Silicate-based yellow-green phosphors

ABSTRACT

Novel phosphor systems are disclosed having the formula A 2 SiO 4 :Eu 2+ D, where A is at least one of a divalent metal selected from the group consisting of Sr, Ca, Ba, Mg, Zn, and Cd; and D is a dopant selected from the group consisting of F, Cl, Br, I, P, S, N, and B. In one embodiment, the novel phosphor has the formula (Sr 1−x−y Ba x M y ) 2 SiO 4 :Eu 2+ F (where M is one of Ca, Mg, Zn, or Cd in an amount ranging from 0&lt;y&lt;0.5). The phosphor is configured to absorb visible light from a blue LED, and luminescent light from the phosphor plus light from the blue LED may be combined to form white light. The novel phosphors can emit light at intensities greater than either conventionally known YAG compounds, or silicate-based phosphors that do not contain the inventive dopant ion.

REFERENCE TO RELATED APPLICATION

The present application is a continuation-in-part of U.S. patentapplication Ser. No. 10/948,764, now U.S. Pat. No. 7,311,858, filed Sep.22, 2004, and titled “Novel silicate-based yellow-green phosphors”,which is a continuation in part of U.S. patent application Ser. No.10/912,741, now U.S. Pat. No. 7,267,787, filed Aug. 4, 2004, and titled“Novel phosphor systems for a white light emitting diode (LED).” U.S.patent applications Ser. No. 10/912,741 (now U.S. Pat. No. 7,267,787)and 10/948,764 (now U.S. Pat. No. 7,311,858) are hereby incorporated byreference in their entirety.

BACKGROUND OF THE INVENTION

1. Field of the Invention

Embodiments of the present invention are directed in general to novelsilicate-based yellow and/or green phosphors (herein referred to asyellow-green phosphors) for use in a white light illumination systemsuch as a white light emitting diodes (LED). In particular, theyellow-green phosphors of the present invention comprise asilicate-based compound having at least one divalent alkaline earthelement and at least one anion dopant, wherein the optical performanceof the novel phosphors is equal to or exceeds that of either knownYAG:Ce compounds or known silicate-based compounds that do not takeadvantage of the benefits of including an anion dopant.

2. State of the Art

White LED's are known in the art, and they are relatively recentinnovations. It was not until LED's emitting in the blue/ultravioletregion of the electromagnetic spectrum were developed that it becamepossible to fabricate a white light illumination source based on an LED.Economically, white LED's have the potential to replace incandescentlight sources (light bulbs), particularly as production costs fall andthe technology develops further. In particular, the potential of a whitelight LED is believed to be superior to that of an incandescent bulbs inlifetime, robustness, and efficiency. For example, white lightillumination sources based on LED's are expected to meet industrystandards for operation lifetimes of 100,000 hours, and efficiencies of80 to 90 percent. High brightness LED's have already made a substantialimpact on such areas of society as traffic light signals, replacingincandescent bulbs, and so it is not surprising that they will soonprovide generalized lighting requirements in homes and businesses, aswell as other everyday applications.

There are several general approaches to making a white lightillumination system based on light emitting phosphors. To date, mostwhite LED commercial products are fabricated based on the approach shownin FIG. 1, where light from a radiation source does affect the coloroutput of the white light illumination. Referring to the system 10 ofFIG. 1, a radiation source 11 (which may be an LED) emits light 12, 15in the visible portion of the electromagnetic spectrum. Light 12 and 15is the same light, but is shown as two separate beams for illustrativepurposes. A portion of the light emitted from radiation source 11, light12, excites a phosphor 13, which is a photoluminescent material capableof emitting light 14 after absorbing energy from the source 11. Thelight 14 can be a substantially monochromatic color in the yellow regionof the spectrum, or it can be a combination of green and red, green andyellow, or yellow and red, etc. Radiation source 11 also emits bluelight in the visible that is not absorbed by the phosphor 13; this isthe visible blue light 15 shown in FIG. 1. The visible blue light 15mixes with the yellow light 14 to provide the desired white illumination16 shown in the figure.

A known yellow phosphor that has been used in the art according to thescheme illustrated in FIG. 1 is a YAG-based phosphor having a mainemission peak wavelength that varies in the range of about 530 to 590 nmdepending on the composition, especially the amount of gadolinium (Gd)atoms substituting yttrium (Y) atoms constituting the YAG-basedphosphor. Another factor that influences the main emission peakwavelength is the amount of the Ce³⁺ added as a luminescent center. Itis known that the peak emission wavelength shifts to longer wavelengthsas either the substitution amount of Gd or the amount of Ce³⁺ isincreased. Color control of the white light may be accomplished bychanging the output ratio between the blue light emitted by the blue LEDand the yellow light emitted by the YAG-based phosphor.

U.S. Pat. No. 5,998,925 to Shimizu et al. discloses the use of a 450 nmblue LED to excite a yellow phosphor comprising ayttrium-aluminum-garnet (YAG) fluorescent material. In this approach aInGaN chip functions as a visible, blue-light emitting LED, and a ceriumdoped yttrium aluminum garnet (referred to as “YAG:Ce”) serves as asingle phosphor in the system. The phosphor typically has the followingstoichiometric formula: Y₃Al₅O₁₂:Ce³⁺. The blue light emitted by theblue LED excites the phosphor, causing it to emit yellow light, but notall the blue light emitted by the blue LED is absorbed by the phosphor;a portion is transmitted through the phosphor, which then mixes with theyellow light emitted by the phosphor to provide radiation that isperceived by the viewer as white light.

The YAG:Ce phosphors of the prior art have known disadvantages. Onedisadvantage is that when used in an illumination system it maycontribute to production of white light with color temperatures rangingfrom 6,000 to 8,000 K, which is comparable to sunlight, and a typicalcolor rendering index (CRI) of about 70 to 75. These specifications areviewed as a disadvantage because in some instances white lightillumination systems with a lower color temperature are preferred, suchas between about 3000 and 4100 K, and in other cases a higher CRI isdesired, such as above 90. Although the color temperature of this typeof prior art system can be reduced by increasing the thickness of thephosphor, the overall efficiency of the system decreases with such anapproach.

Another yellow phosphor that has been used in the art according to thescheme illustrated in FIG. 2 is a silicate-based phosphor described byT. Maeda et al. in U.S. Patent Application Publication 2004/0104391 A1,published Jun. 3, 2004. In this publication, T. Maeda et al. describe asilicate-based phosphor according to the formula(Sr_(1−a1−b1−x)Ba_(a1)Ca_(b1)Eu_(x))₂SiO₄, where 0≦a1≦0.3; 0≦b1≦0.8; and0<x<1. This yellow-yellowish phosphor emits a fluorescence having a mainemission peak in the wavelength range from 550 to 600 nm, inclusive,with a wavelength range 560 to 590 nm being preferred. Still morepreferable was a phosphor emitting a fluorescence having a main emissionpeak in the wavelength range 565 to 585 nm, both inclusive.

That the YAG-based phosphors exemplified by U.S. Pat. No. 5,998,925 toShimizu et al., or the silicate-based phosphors of T. Maeda et al. inU.S. Patent Application Publication 2004/0104391 A1, can produce whitelight according to the visible excitation source scheme of FIG. 1, maybe understood in part by studying an excitation spectra shown in FIG. 2,taken from the Maeda et al. patent application. FIG. 2 is a graphshowing the excitation and emission spectra of Maeda et al.'s silicatephosphor and a YAG-based phosphor. Maeda et al.'s silicate basedphosphor is a yellow (or yellow/yellowish, as they describe it) phosphorwhich has an excitation peak around 250 to 300 nm, and absorbs light ina wavelength range of 100 to 500 nm to emit a yellow/yellowishfluorescence having an emission peak in the 550 to 600 nm range; i.e.,from yellow-green to yellow to orange. Accordingly, if light from theyellow/yellowish phosphor of Maeda et al. is combined with the bluelight from a blue-light-emitting device, the resulting light issubstantially white in nature.

Maeda et al. concede in FIG. 2 that their silicate phosphor has a lowluminous efficacy, the luminous efficacy of their silicate-basedphosphor being only half of that of a YAG-based phosphor under 470 nmexcitation when the silicate-based phosphor is excited by blue light inthe wavelength range greater than 430 nm and less than or equal to 500nm. This necessitates the use of a larger amount of Maeda et al.'sphosphor relative to a YAG-based phosphor in order to obtain the samecolor of light according to the scheme of FIG. 2. In a descriptionprovided by Maeda et al., the luminescent layer is “relatively thick”compared to that which would have been used had the luminescent been aYAG-based phosphor. In this case the blue light intensity used as a partof white illumination will be significantly reduced by relative thicklayer of Maeda et al's yellow phosphors.

What is needed is an improvement over the silicate-based, yellowphosphors of the prior art where the improvement is manifested at leastin part by an equal or greater conversion efficiency from blue toyellow. The enhanced yellow phosphor with low gravity density and lowcost may be used in conjunction with a blue LED to generate light whosecolor output is stable, and whose color mixing results in the desireduniform, color temperature and color rendering index.

SUMMARY OF THE INVENTION

Embodiments of the present invention are directed to novelsilicate-based yellow and/or green phosphors (herein referred to asyellow-green phosphors) for use in a white light illumination systemsuch as a white light emitting diodes (LED). In particular, theyellow-green phosphors of the present invention comprise asilicate-based compound having at least one divalent alkaline earthelement and at least one anion dopant, wherein the optical performanceof the novel phosphors is equal to or exceeds that of either knownYAG:Ce compounds or known silicate-based compounds that do not takeadvantage of the benefits of including an anion dopant.

In one embodiment of the present invention, the novel silicate-basedyellow-green phosphor has the formula A₂SiO₄:Eu²⁺D, where A is at leastone of a divalent metal selected from the group consisting of Sr, Ca,Ba, Mg, Zn, and Cd; and D is a dopant selected from the group consistingof F, Cl, Br, I, P, S, N, and B wherein D is present in the phosphor inan amount ranging from about 0.01 to 20 mole percent. It will beunderstood that not all of these dopants need be present at the sametime; in fact, there may be only one type of dopant, or a combination oftwo or more types of dopants. This silicate-based phosphor is configuredto absorb radiation in a wavelength ranging from about 280 nm to 490 nm,and emits visible light having a wavelength ranging from about 460 nm to590 nm.

In an alternative embodiment, the silicate-based phosphor has theformula (Sr_(1−x−y)Ba_(x)M_(y))₂ SiO: Eu²⁺D, where M is at least one ofan element selected from the group consisting of Ca, Mg, Zn, and Cd, andwhere

0<x<1;

0<y<1 when M is Ca;

0<y<1 when M is Mg; and

0<y<1 when M is selected from the group consisting of Zn and Cd.

In one embodiment, the “D” ion in the silicate-based phosphor ischlorine, sulfur, and/or nitrogen.

In an alternative embodiment, the silicate-based has the formula(Sr_(i−x−y)Ba_(x)M_(y))₂ SiO₄: Eu²⁺Cl,S,N,B, where M is at least one ofan element selected from the group of Ca, Mg, Zn,Cd, where the totalamount of Cl, S, N, and B ranges from 0.0001-.02, and where

0<x<0.3;

0<y<0.5 when M is Ca;

0<y<0.1 when M is Mg; and

0<y<0.5 when M is selected from the group consisting of Zn and Cd.

This phosphor emits light in the yellow region of the electromagneticspectrum, and has a peak emission wavelength ranging from about 540 to590 nm. Again, the nomenclature is mean to convey that at least one typedopant is present; or a combination of dopants, and not all (even morethan one type) need be present.

In an alternative embodiment, the silicate-based phosphor has theformula (Sr_(1−x−y)Ba_(x)M_(y))₂ SiO₄: Eu²⁺Cl,S,N,B, where M is at leastone of an element selected from the group consisting of Ca, Mg, Zn andCd, where the total amount of

Cl, S, N, and B ranges from 0.0001-.02, and where

0.3<x<1;

0<y<0.5 when M is Ca;

0<y<0.1 when M is Mg; and

0<y<0.5 when M is selected from the group consisting of Zn and Cd.

This silicate-based phosphor emits light in the green region of theelectromagnetic spectrum, and has a peak emission wavelength rangingfrom about 500 to 540 nm. The silicate-based phosphor emits light in thegreen region of the electromagnetic spectrum, and has a peak emissionwavelength ranging from about 500 to 530 nm.

In an alternative embodiment, a white light LED is disclosed, the whitelight LED comprising a radiation source configured to emit radiationhaving a wavelength ranging from about 410 to 500 nm; a yellow phosphoraccording to claim 2, the yellow phosphor configured to absorb at leasta portion of the radiation from the radiation source and emit light witha peak intensity in a wavelength ranging from about 530 to 590 nm.

In an alternative embodiment, the white LED may comprise a radiationsource configured to emit radiation having a wavelength ranging fromabout 410 to 500 nm; a yellow phosphor according to claim 2, the yellowphosphor configured to absorb at least a portion of the radiation fromthe radiation source and emit light with peak intensity in a wavelengthranging from about 530 to 590 nm; and a green phosphor according toclaim 1, the green phosphor configured to absorb at least a portion ofthe radiation from the radiation source and emit light with peakintensity in a wavelength ranging from about 500 to 540 nm.

In an alternative embodiment, the white LED may comprise a radiationsource configured to emit radiation having a wavelength ranging fromabout 410 to 500 nm; a green phosphor according to claim 1, the greenphosphor configured to absorb at least a portion of the radiation fromthe radiation source and emit light with peak intensity in a wavelengthranging from about 500 to 540 nm; and a red phosphor selected from thegroup consisting of CaS:Eu²⁺, SrS:Eu²⁺, MgO*MgF*GeO:Mn⁴⁺, andM_(x)Si_(y)N_(z):Eu⁺², where M is selected from the group consisting ofCa, Sr, Ba, and Zn; Z=⅔x+ 4/3y, wherein the red phosphor is configuredto absorb at least a portion of the radiation from the radiation sourceand emit light with peak intensity in a wavelength ranging from about590 to 690 nm. Newer red phosphors include nitridosilicates,aluminonitridosilicates, oxynitridosilicates, andoxynitridoaluminosilicates. One general formula is M_(x)Si_(y)N_(z):Eu²⁺where M is selected from the group consisting of Ca, Sr, Ba, and Zn; andZ=⅔x+ 4/3y. Other examples include:

M₂Si₅N₈:Eu²⁺, where M is Ca, Sr, and Ba;

CaSiN₂:Eu²⁺

CaAlSiN₃:Eu²⁺

(Ca_(1−x−y−z)Sr_(x)Ba_(y)Mg_(z))_(1−n)(Al_(1−a+b)B_(a))Si_(1−b)N_(3−b)O_(b):RE_(n),where 0≦x≦1, 0≦y≦1, 0≦z≦1, 0≦a≦1, 0<b≦1, 0.002≦n≦0.2, and RE is selectedfrom the group consisting of Eu²⁺ and Ce³⁺.

In an alternative embodiment, the white LED may comprise a radiationsource configured to emit radiation having a wavelength ranging fromabout 410 to 500 nm; a yellow phosphor according to claim 2, the yellowphosphor configured to absorb at least a portion of the radiation fromthe radiation source and emit light with a peak intensity in awavelength ranging from about 540 to 590 nm; and a red phosphor selectedfrom the group consisting of CaS:Eu²⁺, SrS:Eu²⁺, MgO*MgF*GeO:Mn⁴⁺, andM_(x)Si_(y)N_(z):Eu⁺², where M is selected from the group consisting ofCa, Sr, Ba, and Zn; and Z=⅔x+ 4/3y, and the newer red phosphorsdescribed above, wherein the red phosphor is configured to absorb atleast a portion of the radiation from the radiation source and emitlight with peak intensity in a wavelength ranging from about 590 to 690nm.

Further embodiments of the composition comprise a silicate-based yellowphosphor having the formula A₂SiO₄:Eu²⁺D, wherein A is at least onedivalent metal selected from the group consisting of Sr, Ca, Ba, Mg, Zn,and Cd; and D is an ion that is present in the yellow phosphor in anamount ranging from about 0.01 to 20 mole percent; and a blue phosphor;wherein the yellow phosphor is configured to emit visible light with apeak intensity in a wavelength ranging from about 540 nm to 590 nm; andthe blue phosphor is configured to emit visible light with a peakintensity in a wavelength ranging from about 430 to 510 nm. The bluephosphor of the composition is selected from the group consisting ofsilicate-based phosphors and aluminate-based phosphors. The compositionof the silicate-based blue phosphor may have the formulaSr_(i−x−y)Mg_(x)Ba_(y)SiO₄:Eu²⁺F; and where

0.5<x<1.0; and

0<y<0.5.

Alternatively, the composition of the aluminate-based blue phosphor mayhave the formula Sr_(i−x)MgEu_(x)A1 ₁₀O₁₇; and where

0.01<x<1.0.

In an alternative embodiment, a composition comprises a silicate-basedgreen phosphor having the formula A₂SiO₄:Eu²⁺D, wherein A is at leastone of a divalent metal selected from the group consisting of Sr, Ca,Ba, Mg, Zn, and Cd; and D is a negatively charged halogen ion that ispresent in the yellow phosphor in an amount ranging from about 0.01 to20 mole percent; a blue phosphor; and a red phosphor; wherein the greenphosphor is configured to emit visible light with a peak intensity in awavelength ranging from about 500nm to 540 nm; the blue phosphor isconfigured to emit visible light with a peak intensity in a wavelengthranging from about 430 to 510 nm; and the red phosphor is configured toemit visible light with a peak intensity in a wavelength ranging fromabout 575 to 690 nm.

In an alternative embodiment, methods are provided for preparing asilicate-based yellow phosphor having the formula A₂SiO₄:Eu²⁺D, whereinA is at least one of a divalent metal selected from the group consistingof Sr, Ca, Ba, Mg, Zn, and Cd; and D is a dopant selected from the groupconsisting of F, Cl, Br, I, P, S, N, and B, wherein D is present in thephosphor in an amount ranging from about 0.01 to 20 mole percent, themethod selected from the group consisting of a sol-gel method and asolid reaction method.

Methods for preparing the novel phosphors include sol-gel methods, whichcomprises the steps of:

a) dissolving a desired amount of an alkaline earth nitrate selectedfrom the group consisting of Mg, Ca, Sr, and Ba-containing nitrates withEu₂O₃ and a compound selected from the group consisting of BaF₂, NH₄F,an alkaline earth metal halide, and an ammonium halide, in an acid, toprepare a first solution;

b) dissolving corresponding amount of a silica gel in de-ionized waterto prepare a second solution;

c) stirring together the solutions produced in steps a) and b), and thenadding ammonia to generate a gel from the mixture solution;

d) adjusting the pH of the solution produced in step c) to a value ofabout 9, and then stirring the solution continuously at about 60° C. forabout 3 hours;

e) drying the gelled solution of step d) by evaporation, and thendecomposing the resulting dried gel at 500 to 700° C. for about 60minutes to decompose and acquire product oxides;

f) cooling and grinding the gelled solution of step e) to produce apowder;

g) calcining/sintering the powder of step f) in a reduced atmosphere forabout 6 to 10 hours, wherein the sintering temperature ranged from about1200 to 1400° C.

In a method that involves a solid reaction method, the steps comprise:

a) wet mixing desired amounts of alkaline earth oxides or carbonates(Mg, Ca, Sr, Ba), Eu₂O₃, and a dopant selected from the group consistingof BaF₂, NH₄F, an alkaline earth metal halide, and ammonium halide, andcorresponding SiO₂;

b) after drying and grinding, calcining and sintering the resultingpowder in a reduced atmosphere for about 6 to 10 hours, wherein thecalcining/sintering temperature ranged from about 1200 to 1400° C.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is a schematic representation of a general scheme forconstructing a white light illumination system, the system comprising aradiation source that emits in the visible, and a phosphor that emits inresponse to the excitation from the radiation source, wherein the lightproduced from the system is a mixture of the light from the phosphor andthe light from the radiation source;

FIG. 2 is an excitation spectrum plotted as a function of wavelength fora prior art YAG-based phosphor and a prior art silicate-based phosphor;included in the graph is an emission spectra measured from each of twoprior art yellow phosphors, where both have been excited with radiationhaving a wavelength of 470 nm;

FIG. 3 shows a collection of emission spectra of exemplary phosphorsaccording to the embodiments of the present invention, the compositionsvarying in fluorine content but conforming to the formula[(Sr_(0.7)Ba_(0.3))_(0.98)Eu_(0.02)]₂SiO_(4−x)F_(x), where thewavelength of the excitation radiation used in the experiment was about450 nm;

FIG. 4 is a graph of emission intensities versus doping concentration ofthe ion (D) for exemplary compositions having the formula[(Sr_(0.7)Ba_(0.3))_(0.98)Eu_(0.02)]₂SiO_(4−x)D_(x), where D in thisexperiment is F, Cl, or P;

FIG. 5 is a graph of the peak wavelength position versus dopingconcentration of the anion (D) for exemplary compositions having theformula [(Sr_(0.7)Ba_(0.3))_(0.98)Eu_(0.02)]₂SiO_(4−x)D_(x), where D inthis experiment is F, Cl, or P;

FIG. 6 is a graph of the excitation spectra comparing fluorinecontaining silicates and non-fluorine containing silicates, furtherconfirming the role that fluorine plays in the present embodiments;

FIG. 7 shows a collection of emission spectra for exemplary phosphorshaving the formula [(Sr_(1−x)Ba_(x))_(0.98)Eu_(0.02)]₂SiO_(4−y)D_(y),illustrating how both peak intensity and wavelength position change as afunction of the ratio of the two alkaline earths Sr and Ba;

FIG. 8 is a graph of emission intensity as a function of wavelength forcompounds having similar CIE color, including novel phosphors preparedby mixing 40% [(Sr_(0.7)Ba_(0.3))_(0.98)Eu_(0.02)]₂SiO_(3.9)F_(0.1) and60% [(Sr_(0.9)Ba_(0.05)Mg_(0.05))_(0.98)Eu_(0.02)]₂SiO_(3.9)F_(0.1);

FIG. 9 is a collection of emission spectra of the exemplary phosphor[(Sr_(0.7)Ba_(0.3))_(0.98)Eu_(0.02)]₂SiO_(3.9)F_(0.1) tested as afunction of temperature, which ranged from 25 to 120° C.;

FIG. 10 is a graph of the maximum intensities of the spectra plotted asa function of temperature, where the maximum intensity of the exemplaryyellow phosphor [(Sr_(0.7)Ba_(0.3))_(0.98)Eu_(0.02)]₂SiO_(3.9)F_(0.1) isshown compared with a YAG:Ce compound and a (Y,Gd)AG compound;

FIG. 11 is a graph of the maximum emission wavelengths of the spectrashown in FIG. 8 plotted as a function of temperature for the exemplaryyellow phosphor [(Sr_(0.7)Ba_(0.3))_(0.98)Eu_(0.02)]₂SiO_(3.9)F_(0.1);

FIG. 12 is a graph of the maximum emission intensity as a function ofhumidity for the exemplary yellow-green phosphor[(Sr_(0.7)Ba_(0.3))_(0.98)Eu_(0.02)]₂SiO_(3.9)F_(0.1);

FIG. 13 relates to fabrication of the novel yellow-green phosphor, andis a graph of the fluorine concentration of a starting material in anexemplary sintered phosphor as a function of the mole percent offluorine that actually ends up in the phosphor, the fluorine content inthe sintered phosphor measured by secondary ion emission spectroscopy(SIMS);

FIG. 14 shows the location of the inventive yellow-green phosphors on aCIE diagram, along with an exemplary YAG:Ce phosphor for comparison;

FIG. 15 is an emission spectrum from an exemplary white LED comprisingyellow light from an exemplary(Sr_(0.7)Ba_(0.3)Eu_(0.02))_(1.95)Si_(1.02)O_(3.9)F_(0.1) phosphor incombination with blue light from a blue LED (used to provide excitationradiation to the exemplary yellow-green phosphor), the excitationwavelength of the blue LED about 450 nm;

FIG. 16 is an emission spectrum from an exemplary white LED comprisingyellow light from the exemplary(Sr_(0.7)Ba_(0.3)Eu_(0.02))_(1.95)Si_(0.02)O_(3.9)F_(0.1) phosphor incombination with green light from an exemplary green phosphor having theformula (Ba_(0.3)Eu_(0.02))_(1.95)Si_(1.02)O_(3.9)F_(0.1), with bluelight from the blue LED as before in FIG. 14, the excitation radiationfrom the blue LED again having a wavelength of about 450 nm;

FIG. 17 is an emission spectrum from an exemplary white LED comprising ablue LED (emitting at a peak wavelength of about 450 nm), the inventiveyellow-green phosphor this time adjusted to emit more in the green atabout 530 nm, and a red phosphor having the formula CaS:Eu;

FIG. 18 is a chromaticity diagram showing the positions of an exemplaryred, green and yellow phosphor, and the position of the resulting whitelight created by mixing light from the individual phosphors.

DETAILED DESCRIPTION OF THE INVENTION

Embodiments of the present invention will be described in the followingorder: first, a general description of the novel silicate-based phosphorwill be given, particularly with respect to selection of the dopantanion and reasons for its inclusion, and benefits especially in terms ofenhanced emission intensity; the alkaline earths present in thephosphor, and the effect their content ratios has on luminescentproperties; and the effects that temperature and humidity have on thephosphor. Next, phosphor processing and fabrication methods will bediscussed. Finally, the white light illumination that may be producedusing the novel yellow-green phosphor will be disclosed by firstdiscussing the general characteristics of a blue LED, followed by adiscussion of other phosphors that may be used in tandom with the novelyellow-green phosphor, such as, in particular, a red phosphor.

The Novel Yellow Phosphors of the Present Embodiments

According to embodiments of the present invention, a yellow phosphorhaving the formula A₂SiO₄:Eu²⁺D is disclosed, wherein A is at least oneof a divalent metal selected from the group consisting of Sr, Ca, Ba,Mg, Zn, and Cd; and D is a negatively charged ion, present in thephosphor in an amount ranging from about 0.01 to 20 mole percent. Theremay be more than one of the divalent metal A present in any onephosphor. In a preferred embodiment, D is a dopant ion selected from thegroup consisting of F, Cl, Br, and I, but D can also be an element suchas N, S, P, As, Sb, and B. The silicate-based phosphor is configured toabsorb an excitation radiation having a wavelength ranging from about280 nm to 520 nm, and particularly from wavelengths in the visibleportion of that range such as from 430 to 480 nm. For example, thepresent silicate-based phosphor is configured to emit visible lighthaving a wavelength ranging from about 460 nm to 590 nm, and has theformula (Sr_(1−x−y)Ba_(x)Ca_(y)Eu_(0.02))₂SiO_(4−z)D_(z); and where0<x<1.0, 0<y<0.8., and 0<z<0.2. An alternative formula is(Sr_(1−x−y)Ba_(x)Mg_(y)Eu₀₀₂)₂SiO_(4−z)D_(z), where 0<x<1.0, 0<y<0.2,and 0<z<0.2. In an alternative embodiment, the phosphor may be describedby the formula (Sr_(1−x−y)Ba_(x)M_(y))₂ SiO₄: Eu²⁺D, where 0<x<1, and Mis one or more of Ca, Mg, Zn, Cd. In this embodiment, the condition0<y<0.5 applies when M is Ca; 0<y<0.1 when M is Mg; and 0<y<0.5 when Mis either Zn or Cd. In a preferred embodiment, the component D is theelement fluorine (F).

Exemplary phosphors were fabricated according to the presentembodiments, and characterized optically in a variety of ways. First,and perhaps most revealing, were tests conducted to evaluate theintensity of the light emitted from the phosphor as a function ofwavelength, wherein the test was carried out on a series of phosphorcompositions that varied in the content of the D anion. From this data,it is useful to construct a graph of peak emission intensities, as afunction of D anion content. Also useful is the construction of a graphof peak emission wavelength, again as a function of D anion content.Finally, it is possible to investigate the role that the divalent metalplays in phosphor performance; specifically, a series of compositionsmay be fabricated that contain two alkaline earth elements A₁ and A₂,sometime with an additional (or third) alkaline earth element A₃, andemission spectra as a function of wavelength may be measured for thedifferent alkaline earths. In the case of two alkaline earths, in otherwords, the ratio of A₁/A₂ content may be varied.

Exemplary data is shown in FIGS. 3-6. The phosphor chosen to illustratethe inventive concept was a yellow-green phosphor of the family[(Sr_(1−x)Ba_(x))_(0.98)Eu_(0.02)]₂SiO_(4−y)D_(y). In other words, itwill be understood by those skilled in the art that the alkaline earthcomponents (A₁ and A₂) in these exemplary compositions are Sr and Ba;that it is an Eu²⁺ activated system, and that the D anions chosen forthese compositions are F and Cl. Although “D” has been consistentlyreferred to as an anion in this disclosure, it is possible for a cationto be incorporated into the structure. The results of such a compositionare shown as well in FIG. 5, where the inclusion of phosphorus iscompared to the results obtained for chlorine and fluorine.

The effect of the inclusion of the D anion dopant into the phosphor,where D is fluorine (F) in an exemplary composition, is seen in FIGS.3-5. Referring to FIG. 3, the emission spectra was taken of a series ofsix compositions for the composition[(Sr_(0.7)Ba_(0.3))_(0.98)Eu_(0.02)]₂SiO_(4−x)D_(x), where the molepercent (mol %) of the fluorine was 0, 3.2, 13.5, 9.0, 16.8, and 19.0,respectively. The wavelength of the excitation radiation in thisexperiment was 450 nm, and so light from this blue LED may be consideredto contribute to the subsequently produced white light illumination. Theresults of FIG. 3 show that the emission intensity from this phosphor issignificantly increased by doping the compositions with fluorine forconcentrations up to about 10 mol %, at which point the intensity beginsto fall off as the fluorine concentration is increased further.

The data from FIG. 3 may be plotted in a slightly different way: thevalue of the emission intensity at the maximum of each of the peaks maybe plotted as a function of fluorine content, as shown for F using thetriangle symbols in FIG. 4. For example, since the curve in FIG. 3exhibiting the highest intensity occurred for the composition having afluorine content of 9 mol %, the highest point of the F-ion curve inFIG. 4 occurs at a location on the x-axis also at 9 mol %. What makesFIG. 4 interesting (and the reason for plotting the data in thismanner), is that such a plot allows different D anions to be compared.Referring to FIG. 4, normalized peak emission intensities have beenplotted as a function of doping concentration of the anions fluorine(triangles), chlorine (circles), and phosphorus (squares), again wherethe host phosphor comprised a silicate with Sr and Ba alkaline earthcomponents in mole ratio 0.7 and 0.3, respectively.

The data in FIG. 4 shows that the fluorine anion is most capable ofincreasing emission intensity, relative to P and Cl, and in thisparticular system under study. It is interesting to note that the F andP compositions both peaked at about 9 mol %, whereas the Cl emissionintensity was relatively constant over the range 9 to 17 mol %, and mayeven have shown a slight increase over the 9 to 17 mol % range. Itshould also be noted that whereas the increase offered by the Cl and Pcompositions is significant, being about a 40 to 50% in normalizedintensity at an optimized concentration, the advantage may not appear tobe significant only because of the huge increase of 100% that the Fcomposition displayed. Furthermore, there may be advantages offered bythe relatively flat curve of the Cl composition, in this instance, wherefabrication difficulties and/or inconsistencies in content tolerancesmay be ignored because of the relative constant nature of the emissionover a range of compositions (e.g., Cl content ranging from 9 to 17 mol%).

Just as normalized peak emission intensity may be plotted as a functionof doping concentration for a series of D anion or cation (in this case,F, Cl, or P) compositions, so too may the wavelength at which that peakemission occurs be plotted as a function of wavelength. This data isshown in FIG. 5, again for the family of compositions[(Sr_(0.7)Ba_(0.3))_(0.98)Eu_(0.02)]₂SiO_(4−x)D_(x), where D is eitheran F, Cl, or P anion. As before, the wavelength of the excitationradiation was about 450 nm. The results of FIG. 5 show that the peakemission wavelength does not significantly vary with concentration forP, but does decrease for F and Cl with increasing dopant concentrationto a value between about 2 and 4 mol %, steadily increasing thereafter.FIG. 6 is an example of excitation (absorption) spectra from anexemplary phosphor, tested with an excitation wavelength of about 450nm, affected by fluorine content in the inventive silicate basedphosphors. It showed clearly again that the fluorine dramaticallychanged the excitation spectra of silicate phosphors, in particular forthe wavelength range from about 400 nm to 500 nm. This has a tremendousimpact on white LED applications, since the 100 percent increase inexcitation intensity at the excitation wavelength 430 to 490 nm of blueLED was achieved with only about 10 percent increase (mole percent) influorine concentration.

The effects that the inclusion of the D anion component into thephosphor have been discussed in FIGS. 3-5. Before preceeding to adisclosure of the effects of the alkaline earth component, a briefdiscussion of the role that the D anion plays in the composition will begiven.

The Role that the Ion Dopant (D) Plays in the Yellow Phosphor

The effect of the inclusion of the anion D into the phosphor ishighlighted by FIG. 3, which shows a collection of emission spectra ofexemplary yellow phosphors varying in fluorine content. The wavelengthof the excitation radiation used in the experiment was about 450 nm. Inone embodiment, fluorine is added to the phosphor composition in theform of a NH₄F dopant. The present inventors have found that when theNH₄F dopant amount is very small (about 1%), the position of the peakemission is located at shorter wavelengths, and as more NH₄F is added,the wavelength increases with dopant amount. The luminescence of the Eudoped phosphor is due to the presence of the Eu²⁺ in the compound, whichundergoes an electronic transition from 4f⁶5d¹ to 4f⁷. The wavelengthpositions of the emission bands depend very much on the host's materialor crystal structure, changing from the near-UV to the red region of thespectrum. This dependence is interpreted as due to the crystal fieldsplitting of the 5d level. With increasing crystal field strength, theemission bands shift to longer wavelength. The luminescence peak energyof the 5d-4f transition is affected most by crystal parameters denotingelectron-electron repulsion; in other word, the distance between Eu²⁺cation and surrounding anions, and the average distance to distantcations and anions.

In the presence of small amounts of NH₄F, the fluorine anion dopantfunctions predominantly as a flux during sintering processing.Generally, a flux improves sintering processing in one of two ways: thefirst is to promote crystal growth with the liquid sintering mechanism,and the second is to absorb and collect the impurities from the crystalgrains and improve the phase purity of the sintered materials. In oneembodiment of the present invention, the host phosphor is(Sr_(1−x)Ba_(x))₂SiO₄. Both Sr and Ba are very large cations. There maybe present smaller cations such as Mg and Ca, which may be considered tobe impurities. Therefore, further purification of host lattice will leadto more perfect symmetric crystal lattice and a larger distance betweencations and anions, with a result of a weakening of the crystal fieldstrength. This is the reason that small amount doping of NH₄F moves theemission peak to shorter wavelength. The emission intensity increaseswith this small amount of F doping attributes to a higher qualitycrystal with fewer defects.

When the amounts of NH₄F are increased even further, some of the F⁻anions will replace O²⁻ anions, and become incorporated into thelattice. Cation vacancies will be created in order to maintain anelectrical charge neutrality. Since the vacancies in the cationpositions reduce the average distance between cations and anions, thecrystal field strength will be increased. Therefore, the peak of theemission curves will move to longer wavelength as the NH₄F contentincreases due to the increased number of cation vacancies. The emissionwavelength is directly related to the energy gap between ground andexcitation states which is determined only by the crystal fieldstrength. The result of emission wavelength increases with the fluorineand chlorine is strong evidence of fluorine or chlorine incorporatinginto the host lattice, most likely in substitute of oxygen sites. On theother hand, the addition of a phosphate ion does not substantiallychange the emission wavelength, as expected. This is again evidence thatphosphate acts as a cation, will not replace oxygen, and thus will notbe easily incorporated into the lattice to change the host material'scrystal field strength. This is particularly true of the crystal fieldsurrounding the Eu²⁺ ions, which consist essentially of oxygen sites.The improvement in the emission intensity gained by adding NH₄H₂PO₄indicates that it works a flux agent as discussed above.

The excitation spectra comparing fluorine containing silicates andnon-fluorine containing silicates, as shown in FIG. 6, further confirmedthe critical role that fluorine plays in the present embodiments of thepresent halide containing silicate phosphors. The excitation spectrashown in FIG. 6 is obtained by plotting the emission intensity at thewavelength of 540 nm verses an excitation wavelength. The excitationintensity is directly related to the absorption and determined byexcitation and transmission probability between excitation level andground level. The dramatic increase in excitation intensity above 400 nmby introduction of fluorine into the silicate phosphor indicates againstrongly that fluorine incorporates into the silicate lattice andchanged dramatically the symmetrical surrounding of Eu⁺² tononsymmetrical structure, which directly increases the probability ofemission and transmission between emission sate to ground state. FromFIG. 6 one skilled in the art may see that about 10 mol % fluorine insilicate phosphor can increase about 100% emission intensity ofnon-fluorine contained silicate phosphor in the excitation wavelengthfrom 450 to 480 nm which is the most important for white LEDapplications.

The emission intensity decreases or levels off when the halideconcentration increases more than 10 mol % as shown in FIG. 3. This canbe explained by Eu emission quenching due to the fact that more defectsintroduced in associated with the fluorine incorporation into thelattice, the more non-radiation centers will be created to reduce theabsorbed energy transferring to Eu²⁺ effective emission centers. Theresult in FIG. 3 indicates the maximum intensity increase by fluorinewithout Eu emission quenching is about 10 mol %.

Effect of the Alkaline Earth Component

The optical properties of the inventive yellow phosphor may becontrolled, in addition to the methods discussed above, by adjusting theratio of the alkaline earth elements contained within the phosphor. Anexemplary data set that puts this embodiment of the inventive conceptinto place is illustrated in FIG. 7. Before turning to FIG. 7, however,it may be useful to discuss the general effects of typical alkalineearths on the crystal structure of the phosphor, which in turn willaffect optical properties, where the alkaline earths under considerationare Sr, Ba, Ca, and Mg.

T. Maeda et al. do not teach the benefits of the present dopant ion D inU.S. Patent Application Publication 2004/0104391. Many of the principlespertaining to the alkaline earth content, however, still apply. Maeda etal. teach that when the content of Ba and Ca in a silicate phosphor isvery small; in other words, when the content of the alkaline earths inthe phosphor is mostly Sr, then the phosphor is likely to assume amonoclinic structure, or a structure comprising a mixture of monoclinicand orthorhombic crystal structures. When Ba is put into the phosphor athigher values than desired with little or no Ca, the crystal fieldaround Eu²⁺ions is weak. If the Ba content is low and the Ca content ishigher than desired, the crystal structure is again likely to bemonoclinic. Finally, if both the Ba and Ca contents are larger thandesired, relative to the amount of Sr in the phosphor, then thesilicate-based phosphor is likely to have a hexagonal structure. In eachof these cases, according to Maeda et al., the phosphor is expected tobe greener, and emits light with a low color purity for yellow.

T. Maeda et al. teach that in order to obtain yellow light from thephosphor, which may be defined as light having a wavelength ranging fromabout 550 to 600 nm, the desired Ba content in the phosphor should be ina mole fraction from about 0 to 0.3. With regard to the Ca content, thedesired condition for obtaining yellow wavelengths lies from about 0 to0.6, although they conjecture that yellow wavelengths may also beobtained from a compound in which the Ca substitution (for Sr) has amole fraction of about 0.7. Maeda et al. note that compounds that do notcontain any Sr do not emit yellow light.

The present inventors have completed an investigation of the compositionspace (Sr_(1−x−y−z)Ba_(x)Ca_(y)Mg_(z))₂SiO₄ (where x+y+z=1) to enhanceluminescent properties. In this case the particular interest was tooptimize the material configured to emit green to yellow color light byblue excitation. The effects of stoichiometric ratio of calcium,strontium and barium on luminescent properties were found in consistentwith Maeda et al's results disclosed in their patent. However, thepresent invention is more focused on the improvements of emissionintensity while controlling the emission wavelength in the desired greento yellow region. FIG. 7 is a graph of the emission spectra of exemplaryyellow-green phosphors belonging to the family[(Sr_(0.7)Ba_(0.3))_(0.98)Eu_(0.02)]₂SiO_(3.9)F_(0.1), where the valueof the strontium content in the series varies from 0 to 12, 25, 37, 50,60, 65, 70, 80, 90, and 100 percent. Plotted another way, the value of xin the formula Sr_(1−x)Ba_(x) ranges from 0, 0.1, 0.2, 0.3, 0.35, 0.4,0.5, 0.63, 0.75, 0.87, and 1.0. Also plotted for comparison is a priorart YAG:Ce phosphor. The present study of the effects of alkaline metalson luminescent properties of silicate phosphors may be summarized asfollows:

-   -   (1) In (Sr_(1−x)Ba_(x))₂SiO₄ phosphor materials, the emission        peak wavelength changes from green at 500 nm for x=1 (100% Ba)        to yellow at 580 nm for x=0 (100% Sr) as shown in FIG. 7. The        conversion efficiency from the same light source at 450 nm shows        a continuous increase when the Ba increases from 0 to about 90%.        The peak emission wavelength of 545 nm obtained when Ba to Sr        ratio is 0.3 to 0.7 is close to the pure YAG:Ce peak emission        wavelength as compared in FIG. 7.    -   (2) Calcium substitution of barium or strontium in the Sr—Ba        based silicate phosphor system will in general reduce the        emission intensity, even they can be favored for moving the        emission to longer wavelength when calcium substitution is less        than 40%.    -   (3) Magnesium substitution of barium or strontium in the Sr—Ba        based silicate phosphors will in general reduce the emission        intensity and move the emission to shorter wavelengths. However,        the small amount of magnesium substitution of barium or        strontium (<10%) will enhance the emission intensity and move        the emission to longer wavelengths. For example, five percent of        substitution of barium by magnesium in (Sr_(0.9)Ba_(0.1))₂SiO₄        will increase the emission intensity and move to a slightly        longer wavelength, as shown in FIG. 7 for the curve labeled        [(Sr_(0.9)Ba_(0.075)Mg_(0.025))_(0.98)Eu_(0.02)]₂SiO_(3.9)F_(0.1).    -   (4) To match or improve upon a YAG emission spectrum, it may be        necessary in some embodiments of the present invention to mix        the inventive silicate phosphors. FIG. 8 shows that a        substantially identical CIE color of YAG can be prepared by        mixing 40% [(Sr_(0.7)Ba_(0.3))_(0.98)Eu_(0.02)]₂SiO_(3.9)F_(0.1)        and 60%        [(Sr_(0.9)Ba_(0.05)Mg_(0.05))_(0.98)Eu_(0.02)]₂SiO_(3.9)F_(0.1).        The total brightness of the mixture is estimated to be nearly        90% as bright as the YAG composition.        Effects of Temperature and Humidity on the Phosphor

Temperature and humidity effects on the luminescent properties are veryimportant to phosphor-based illumination devices such as white LEDs,based on partial or total conversion of LED emission to other wavelengthemissions by the selected phosphor material system. The operatingtemperature range for such phosphor-based radiation devices depends onthe specific application requirements. Temperature stable up to 85° C.are generally required for commercial electronic applications. However,temperatures up to 180° C. are desired for high power LED applications.Stability over the entire humidity range of 0 to 100% is required foralmost all commercial electronic applications.

FIGS. 9-11 are plots of maximum luminescent intensity either as afunction of temperature, or of wavelength for various temperatures, foran exemplary fluorine containing silicate phosphor(Sr_(0.7)Ba_(0.3)Eu_(0.02))_(1.95)Si_(1.02)O_(3.9)F_(0.1). Thisparticular phosphor was derived from the series of emission spectrameasured at different temperatures shown previously. The temperaturestability of the phosphor of this invention behaves very similar to thatof a commercial YAG phosphor, particularly up to 100° C. FIG. 12 showsgraph of the stability of the phosphor of this invention for humidityranging from about 20 to 100%. Without being constrained to any onetheory, the inventors believe that while the reason for the 3% increasein emission maximum intensity above 90% humidity is unknown at thistime, such a phenomena is reversible when the humidity oscillatesbetween a value of about 90% to 100%.

Phosphor Fabrication Processes

Methods of fabricating the novel silicate-based phosphor of the presentembodiments are not limited to any one fabrication method, but may, forexample, be fabricated in a three step process that includes: 1)blending starting materials, 2) firing the starting material mix, and 3)various processes to be performed on the fired material, includingpulverizing and drying. The starting materials may comprise variouskinds of powders, such as alkaline earth metal compounds, siliconcompounds, and europium compounds. Examples of the alkaline earth metalcompounds include alkaline earth metal carbonates, nitrates, hydroxides,oxides, oxalates, and halides. Examples of silicon compounds includeoxides such as silicon oxide and silicon dioxide. Examples of europiumcompounds include europium oxide, europium fluoride, and europiumchloride. As a germanium material for the germanium-containing novelyellow-green phosphors of the present invention, a germanium compoundsuch as germanium oxide may be used.

The starting materials are blended in a manner such that the desiredfinal composition is achieved. In one embodiment, for example, thealkaline-earth, silicon (and/or germanium), and europium compounds arebended in the appropriate ratios, and then fired to achieve the desiredcomposition. The blended starting materials are fired in a second step,and to enhance the reactivity of the blended materials (at any orvarious stages of the firing), a flux may be used. The flux may comprisevarious kinds of halides and boron compounds, examples of which includestrontium fluoride, barium fluoride, calcium fluoride, europiumfluoride, ammonium fluoride, lithium fluoride, sodium fluoride,potassium fluoride, strontium chloride, barium chloride, calciumchloride, europium chloride, ammonium chloride, lithium chloride, sodiumchloride, potassium chloride, and combinations thereof. Examples ofboron-containing flux compounds include boric acid, boric oxide,strontium borate, barium borate, and calcium borate.

In some embodiments, the flux compound is used in amounts where thenumber of mole percent ranges from between about 0.1 to 3.0, wherevalues may typically range from about 0.1 to 1.0 mole percent, bothinclusive.

Various techniques for mixing the starting materials (with or withoutthe flux) include using a mortar, mixing with a ball mill, mixing usinga V-shaped mixer, mixing using a cross rotary mixer, mixing using a jetmill and mixing using an agitator. The starting materials may be eitherdry mixed or wet mixed, where dry mixing refers to mixing without usinga solvent. Solvents that may be used in a wet mixing process includewater or an organic solvent, where the organic solvent may be eithermethanol or ethanol.

The mix of starting materials may be fired by numerous techniques knownin the art. A heater such as an electric furnace or gas furnace may beused for the firing. The heater is not limited to any particular type,as long as the starting material mix is fired at the desired temperaturefor the desired length of time. In some embodiments, firing temperaturesmay range from about 800 to 1600° C. The firing time may range fromabout 10 minutes to 1000 hours. The firing atmosphere may be selectedfrom among air, a low-pressure atmosphere, a vacuum, an inert-gasatmosphere, a nitrogen atmosphere, an oxygen atmosphere, an oxidizingatmosphere, and/or a reducing atmosphere. Since Eu²⁺ ions need to beincluded in the phosphor at some stage of the firing, it is desired insome embodiments to provide a reducing atmosphere using a mixed gas ofnitrogen and hydrogen.

Exemplary methods of preparing the present phosphors include a sol-gelmethod and a solid reaction method. The sol-gel method may be used toproduce powder phosphors. A typical procedure comprised the steps of:

-   1. a) Dissolving certain amounts of alkaline earth nitrates (Mg, Ca,    Sr, Ba), and Eu₂O₃ and/or BaF₂ or other alkaline earth metal halides    in dilute nitric acid; and b) Dissolving corresponding amount of    silica gel in de-ionized water to prepare a second solution.-   2. After the solids of the two solutions of steps 1a) and 1b) above    were totally dissolved, the two solutions were mixed and stirred for    two hours. Ammonia was then used to generate a gel in the mixture    solution. Following formation of the gel, the pH was adjusted to    about 9.0, and the gelled solution stirred continuously at about    60° C. for 3 hours.-   3. After drying the gelled solution by evaporation, the resulted dry    gel was decomposed at 500 to 700° C. for about 60 minutes to    decompose and acquire oxides.-   4. After cooling and grinding with certain amount of NH₄F or other    ammonia halides when alkaline earth metal halides are not used in    step 1a), the powder was sintered in a reduced atmosphere for about    6 to 10 hours. The calcining/sintering temperature ranged from about    1200 to 1400° C.

Alternatively, the solid reaction method was also used forsilicate-based phosphors. The steps of a typical procedure used for thesolid reaction method are as following:

-   1. Desired amounts of alkaline earth oxides or carbonates (Mg, Ca,    Sr, Ba), dopants of Eu₂O₃ and/or BaF₂ or other alkaline earth metal    halides, corresponding SiO₂ and/or NH₄F or other ammonia halides    were wet mixed with a ball mill.-   1. After drying and grinding, the resulting powder was    calcined/sintered in a reduced atmosphere for about 6 to 10 hours.    The calcining/sintering temperature ranged from 1200 to 1400° C.

In a specific example relating to the preparation of the presentphosphors, the concentration of fluorine in the sintered phosphor[(Sr_(1−x)Ba_(x))_(0.98)Eu_(0.02)]₂SiO_(4−y)F_(y) was measured usingsecondary ion emission spectroscopy (SIMS), and the results are shown inFIG. 13. In this experiment, the fluorine was added to the phosphor asNH₄F. The results show that for a mol % of fluorine of about 20 mol % inthe starting material, the sintered phosphor ends up with about 10 mol%. When the content of fluorine in the raw material is about 75 mol %,the content of fluorine in the sintered phosphor is about 18 mol %.

Production of White Light Illumination

The white light illumination that may be produced using the inventive,novel yellow-green phosphor will be discussed in this final portion ofthe disclosure. The first section of this final portion will begin witha description of exemplary blue LED's that may be used to excite theinventive yellow-green phosphor. That the present yellow-green phosphorsare capable of absorbing, and be excited by, light over a large range ofwavelengths, including the blue portion of the visible, is demonstratedby the excitation (absorption) spectra of FIG. 6. Next, a generalizeddescription of the CIE diagram will be provided, along with the locationof the inventive yellow-green phosphor on the diagram, as shown in FIG.14. According to the general scheme of FIG. 1, light from the inventiveyellow-green phosphor may be combined with light from the blue LED tomake white illumination; the results of such an experiment are shown inan emission intensity versus wavelength plot for this system in FIG. 15.The color rendering of the white light may be adjusted with theinclusion of other phosphors in the system, as exemplified by thespectrum of FIG. 16. Alternatively, the inventive phosphor may beadjusted to emit more in the green, and combined with a red phosphor tomake up the phosphor system, which together with the blue light from theblue LED produces the spectrum in FIG. 17. To conclude, the CIE diagramof the resulting white light is shown in FIG. 18.

The Blue LED Radiation Source

According to the present embodiments, the blue light emitting LED emitslight having a main emission peak in the wavelength range greater thanor equal to about 400 nm, and less than or equal to about 520 nm. Thislight serves two purposes: 1) it provides the excitation radiation tothe phosphor system, and 2) it provides blue light which, when combinedwith the light emitted from the phosphor system, makes up the whitelight of the white light illumination.

In an alternative embodiment, the blue LED emits light greater than orequal to about 420 nm, and less than or equal to about 500 nm. In yetanother embodiment, the blue LED emits light greater than or equal toabout 430 and less than or equal to about 480 nm. The blue LEDwavelength may be 450 nm.

The blue light emitting device of the present embodiments is hereindescribed generically as a “blue LED,” but it will be understood bythose skilled in the art that the blue light emitting device may be atleast one of (wherein it is contemplated to have several operatingsimultaneously) a blue light emitting diode, a laser diode, a surfaceemitting laser diode, a resonant cavity light emitting diode, aninorganic electroluminescence device and an organic electroluminescencedevice. If the blue light emitting device is an inorganic device, it maybe a semiconductor selected from the group consisting of a galliumnitride based compound semiconductor, a zinc selenide semiconductor anda zinc oxide semiconductor.

FIG. 6 is an excitation spectrum of the present yellow-green phosphors,showing that these novel phosphors are capable of absorbing radiatingover a range of about 280 to 520 nm, and relevant to the presentembodiments, over a range of about 400 to 520 nm. In preferredembodiments of the present invention, the novel yellow-green phosphorsabsorb radiation (in other words, are capable of being excited byradiation) ranging from 430 to 480 nm. In yet another embodiment, thephosphor absorbs radiation having a wavelength of about 450 nm.

Next, a generalized description of the CIE diagram will be given, alongwith a description of where the present yellow-green phosphors appear onthe CIE diagram.

Chromaticity Coordinates on a CIE Diagram and the CRI

White light illumination is constructed by mixing various or severalmonochromatic colors from the visible portion of the electromagneticspectrum, the visible portion of the spectrum comprising roughly 400 to700 nm. The human eye is most sensitive to a region between about 475and 650 nm. To create white light from either a system of LED's, or asystem of phosphors pumped by a short wavelength LED, it is necessary tomix light from at least two complementary sources in the properintensity ratio. The results of the color mixing are commonly displayedin a CIE “chromaticity diagram,” where monochromatic colors are locatedon the periphery of the diagram, and white at the center. Thus, theobjective is to blend colors such that the resulting light may be mappedto coordinates at the center of the diagram.

Another term of art is “color temperature,” which is used to describethe spectral properties of white light illumination. The term does nothave any physical meaning for “white light” LED's, but it is used in theart to relate the color coordinates of the white light to the colorcoordinates achieved by a black-body source. High color temperatureLED's versus low color temperature LED's are shown at www.korry.com.

Chromaticity (color coordinates on a CIE chromaticity diagram) has beendescribed by Srivastava et al. in U.S. Pat. No. 6,621,211. Thechromaticity of the prior art blue LED-YAG:Ce phosphor white lightillumination system described above are located adjacent to theso-called “black body locus,” or BBL, between the temperatures of 6000and 8000 K. White light illumination systems that display chromaticitycoordinates adjacent to the BBL obey Planck's equation (described atcolumn 1, lines 60-65 of that patent), and are desirable because suchsystems yield white light which is pleasing to a human observer.

The color rendering index (CRI) is a relative measurement of how anillumination system compares to that of a black body radiator. The CRIis equal to 100 if the color coordinates of a set of test colors beingilluminated by the white light illumination system are the same as thecoordinates generated by the same set of test colors being irradiated bya black body radiator.

Turning now to the present yellow-green phosphors, various exemplarycompositions of the novel phosphors were excited with 450 nm radiation,and the positions of their emissions on a CIE diagram are shown in FIG.14. The position of the 450 nm excitation light is also shown, as wellas the position of a YAG:Ce phosphor for comparison.

The yellow to yellow-green color of these exemplary phosphors mayadvantageously be mixed with blue light from the blue LED describedabove (wherein the blue light has a wavelength ranging from about 400 to520 nm in one embodiment, and 430 to 480 nm in another embodiment) toconstruct the white light illumination desired for a multiplicity ofapplications. FIG. 15 shows the results of mixing light from a blue LEDwith an exemplary yellow phosphor, in this case the yellow phosphorhaving the formula(Sr_(0.7)Ba_(0.3)Eu_(0.02))_(1.95)Si_(1.02)O_(3.9)F_(0.1).

It will be understood by those skilled in the art that the presentyellow-green phosphor may be used in conjunction with other phosphors,as part of a phosphor system, whereupon the light emitted from each ofthe phosphors of the phosphor system may be combined with the blue lightfrom the blue LED to construct white light with alternative colortemperatures and color renderings. In particular, green, orange and/orred phosphors disclosed previously in the prior art may be combined withthe present yellow-green phosphor.

For example, U.S. Pat. No. 6,649,946 to Bogner et al. disclosed yellowto red phosphors based on alkaline earth silicon nitride materials ashost lattices, where the phosphors may be excited by a blue LED emittingat 450 nm. The red to yellow emitting phosphors uses a host lattice ofthe nitridosilicate type M_(x)Si_(y)N_(z):Eu, wherein M is at least oneof an alkaline earth metal chosen from the group Ca, Sr, and Ba, andwherein z=⅔ x+ 4/3y. One example of a material composition isSr₂Si₅N₈:Eu²⁺. The use of such red to yellow phosphors was disclosedwith a blue light emitting primary source together with one or more redand green phosphors. The objective of such a material was to improve thered color rendition R9 (adjust the color rendering to red-shift), aswell as providing a light source with an improved overall colorrendition Ra.

Another example of a disclosure of supplementary phosphors, includingred phosphors, that may be used with the present yellow-green phosphorare found in U.S. Patent Application Publication 2003/0006702 toMueller-Mach, which disclosed a light emitting device having a(supplemental) fluorescent material that receives primary light from ablue LED having a peak wavelength of 470 nm, the supplementalfluorescent material radiating light in the red spectral region of thevisible light spectrum. The supplementary fluorescent material is usedin conjunction with a main fluorescent material to increase the redcolor component of the composite output light, thus improving the whiteoutput light color rendering. In a first embodiment, the mainfluorescent material is a Ce activated and Gd doped yttrium aluminumgarnet (YAG), while the supplementary fluorescent material is producedby doping the YAG main fluorescent material with Pr. In a secondembodiment, the supplementary fluorescent material is a Eu activated SrSphosphor. The red phosphor may be, for example, (SrBaCa)₂Si₅N₈: Eu²⁺.The main fluorescent material (YAG phosphor) has the property ofemitting yellow light in response to the primary light from the blueLED. The supplementary fluorescent material adds red light to the bluelight from the blue LED and the yellow light from the main fluorescentmaterial.

U.S. Pat. No. 6,504,179 to Ellens et al. disclose a white LED based onmixing blue-yellow-green (BYG) colors. The yellow emitting phosphor is aCe-activated garnet of the rare earths Y, Tb, Gd, Lu, and/or La, where acombination of Y and Tb was preferred. In one embodiment the yellowphosphor was a terbium-aluminum garnet (TbAG) doped with cerium(Tb₃Al₅O₁₂—Ce). The green emitting phosphor comprised a CaMgchlorosilicate framework doped with Eu (CSEu), and possibly includingquantities of further dopants such as Mn. Alternative green phosphorswere SrAl₂O₄:Eu and Sr₄Al₁₄O₂₅:Eu²⁺.

The novel yellow-green phosphor may be used in a combination of greenand yellow phosphors (Tb₃Al₅O₁₂—Ce).

Although a prior art method disclosed in U.S. Pat. No. 6,621,211 toSrivastava et al was designed to emit white light using a non-visible UVLED, this patent is relevant to the present embodiments because of thesupplementary green, orange, and/or red phosphors used in the phosphorsystem. The white light produced in this method was created bynon-visible radiation impinging on three, and optionally a fourth,phosphor, of the following types: the first phosphor emitted orangelight having a peak emission wavelength between 575 and 620 nm, andpreferably comprised a europium and manganese doped alkaline earthpyrophosphate phosphor according to the formula A₂P₂O₇:Eu²⁺, Mn²⁺.Alternatively, the formula for the orange phosphor could be written(A_(1−x−y)Eu_(x)Mn_(y))₂P₂O₇ where 0<x≦0.2, and 0<y≦0.2. The secondphosphor emits blue-green light having a peak emission wavelengthbetween 495 and 550 nm, and is a divalent europium activated alkalineearth silicate phosphor ASiO:Eu²⁺, where A comprised at least one of Ba,Ca, Sr, or Mb. The third phosphor emitted blue light having a peakemission wavelength between 420 and 480 nm, and comprised either of thetwo commercially available phosphors “SECA,” D₅(PO₄)₃Cl:Eu²⁺, where Dwas at least one of Sr, Ba, Ca, or Mg, or “BAM,” which may be written asAMg₂Al₁₆O₂₇, where A comprised at least one of Ba, Ca, or Sr, orBaMgAl₁₀O₁₇:Eu²⁺. The optional fourth phosphor emits red light having apeak emission wavelength between 620 and 670 nm, and it may comprise amagnesium fluorogermanate phosphor MgO*MgF*GeO:Mn⁴⁺.

The Inventive Yellow Phosphor in Combination with Other Phosphors

In one embodiment of the present invention, a white illumination devicecan be constructed using a GaN based blue LED having a emission peakwavelength ranging about 430 nm to 480 nm, in combination with theinventive yellow phosphor with an emission peak wavelength ranging fromabout 540 nm to 580 nm. FIG. 15 is a combination spectra measured from awhite illumination device, which consists of a blue LED and theinventive yellow phosphor layer. The conversion efficiency and theamount of the phosphor used in the device directly determines the colorcoordination of the white illumination devices in CIE diagram. In thiscase, a color temperature of about 5,000 to 10,000 K with a colorcoordination where X ranges from 0.25 to 0.40 and Y ranges from 0.25 to0.40 can be achieved by combining light from the blue LED with lightfrom the inventive yellow phosphor.

In another embodiment, a white illumination device may be constructedusing a GaN based blue LED having an emission peak wavelength rangingfrom about 430 nm to 480 nm; the inventive yellow phosphor has anemission peak wavelength ranging from about 540 nm to 580 nm; and aninventive green phosphor having an emission peak wavelength ranging fromabout 500 nm to 520 nm. The color rendering of the resulting white lighthas been improved with this solution of mixing green and yellowphosphors. FIG. 16 is a combination spectra measured from a whiteillumination device comprising the light from a blue LED, and the lightfrom a mixture of the inventive yellow and green phosphors. Theconversion efficiency and the amounts of the phosphors used in thedevice directly determine the color coordination of the whiteillumination devices in CIE diagram. In this case, a color temperatureof 5,000 to 7,000 K with a color rendering greater than 80 was achievedby combining light from the blue LED with light from a mixture of theinventive yellow and green phosphors.

In another embodiment, a white illumination device may be constructed byusing a GaN based blue LED having an emission peak wavelength rangingfrom about 430 nm to 480 nm; the inventive green phosphor having anemission peak wavelength ranging from about 530 nm to 540 nm; and acommercially available red phosphor such as Eu doped CaS having anemission peak wavelength ranging from 600 nm to 670 nm. The colortemperature may be adjusted to 3,000 K, and color rendering may beenhanced to a value greater than about 90 using the presently disclosedgreen and red phosphors. FIG. 17 is a combination spectra measured froma white illumination device comprising a blue LED and the mixture of theinventive green and CaS:Eu phosphors. The conversion efficiency andamount of the phosphor used in the device directly determines the colorcoordination of the white illumination devices in CIE diagram. In thiscase the color temperature of 2,500 to 4,000 K with color renderinggreater than 85 can be achieved by combining light from the blue LEDwith light from a mixture of the inventive red and green phosphorsystem. FIG. 18 shows the position of the resultant white lightillumination on a CIE diagram.

The Present Yellow-Green Silicates with New Nitride-Based Red Phosphorsin White LEDs

The present yellow-green silicates may be advantageously combined withthe newer, nitride-based “deep-red” phosphors in white LED systems. Thepositions of these new nitrides on the CIE chromaticity diagram, lyingas they do at very long red wavelengths, even approaching the nearinfrared, nicely complement the yellow-green emissions of the presentoxygen substituted phosphors and the blue light from, for example, anysuitable II-V, II-VI, or IV-IV semiconducting diode. The resultant whitelight has better color rendering characteristics, to name one advantage.

Earlier versions of these deep red phosphors were based on nitrides ofsilicon, and hence may be generically referred to as “nitride-based”silicates or nitridosilicates. Newer versions have included aluminum toprovide the compounds “nitridoaluminosilicate nitrides.” The inclusionof oxygen into these crystals, deliberate or otherwise, may also give tothe desired deep red phosphors, even though similar compounds known as“SiAlONs” in some cases are sources of green and yellow-greenillumination. When oxygen substitutes for nitrogen the resultingcompound is an “oxynitrides.”

As alluded to earlier, a combination of LED-generated blue light, andphosphor-generated light, may be used to produce the white light from aso-called “white LED.” The phosphor-generated light, according to thepresent embodiments, comprises both a yellow-green light from one of thesilicate-based yellow-green phosphors described above, and one of thenewer “deep red” type phosphors generally having a nitride hoststructure, such a structure optionally having aluminum (Al) partiallyreplacing silicon (Si) in one embodiment, and oxygen (O) partiallyreplacing nitrogen (N) in another. Nitrides and oxynitrides, each withand without aluminum, are contemplated by the present embodiments. Ablue emitting LED, such as one providing excitation radiation rangingfrom about 400 to 480 nm, is deemed to be particularly suitable forexciting both the yellow-green and the red phosphors.

Previously known white light generating systems used a blue LED inconjunction with a yellow emitting, cerium-doped, yttrium aluminumgarnet known as “YAG,” having the formula Y₃Al₅O₁₂:Ce³⁺. Such systemshave correlated temperatures (CCTs) of greater than about 4,500 K, andcolor rendering indexes (CRIs) ranging from about 75 to 82. It isbelieved the present embodiments provide general illumination sourceshaving higher CRIs and lower CCTs. One method of achieving thisflexibility of design in blue LED-based devices is to provide a widerseparation of the yellow-green and red phosphors relative to one anotherin CIE space, where these two apexes of a triangle formed with the lightfrom the blue LED create a rich diversity of components for white lightgeneration.

As described in U.S. Pat. No. 7,252,787 to D. Hancu et al., deep redsources were used with YAG and TAG-based yellow sources to produce ahigh color rendering index have included nitrides having the formula(Ba,Sr,Ca)_(x)Si_(y)N_(z):Eu²⁺, where each of the x, y, and z parameterswas greater than zero. A disadvantage of such phosphors used withYAG/TAG was that they reabsorb emissions from those phosphors due tooverlapping of the Eu²⁺ absorption bands with the emission of the(Tb,Y)₃Al₅O₁₂:Ce³⁺) phosphors. Thus, there is a need for red phosphorshaving a redder emission than these nitrides to produce white lightillumination with high CRI.

Host lattices for new red-emitting phosphors based on nitridosilicatecompounds were introduced in the mid-1990's. Such phosphors havedesirable mechanical and thermal properties due to a three dimensionalnetwork of cross-linked SiN4 tetrahedra in which alkali earth ions(M=Ca, Sr, and Ba) are incorporated. The formula used in U.S. Pat. No.6,649,946 to Bogner et al. to describe such phosphors was MxSi_(Y)Nz,where M was at least one of an alkaline earth metal, and where z=2/x+4/3y. The nitrogen of these nitrides increased the content of covalentbonding, and thus ligand-field splitting. This lead to a pronouncedshift of excitation and emission bands to longer wavelengths incomparison to oxide lattices.

The effect of the alkaline earth component of such nitridosilicates wheny is 5 was investigated by Y. Q. Li et al. in “Luminescence propertiesof red-emitting M₂Si₅N₈:Eu²⁺ (M=Ca, Sr, Ba) LED conversion phosphors,”J. of Alloys and Compounds 417 (2006), pp. 273-279. Polycrystallinepowders were prepared by a solid state reaction mechanism. The crystalstructure of the Ca-containing member of this family was monoclinic withspace group Cc, whereas the Sr and Ba members were isostructral(orthorhombic with space group Pmn2₁), with the formation of a completesolid solution between the Sr and Ba end-members.

The position of the 5d excitation bands of the Eu²⁺ ions in thesecompounds at low energies is attributable to the influence of the highlycovalent nature of the europium on an alkaline earth metal site withnitrogen atoms, leading to a large crystal field splitting, as well,also due to the presence of nitrogen. The covalency of the Eu—N bond andthe resultant crystal field strength around the Eu²⁺ ions is similar ineach of the members of this series (e.g., Ca, Sr, and Ba-based), despitethe fact there are two M sites with different symmetries. Of particularimportance to white LEDs is the fact these compounds have efficientexcitation in the same spectral region (400 to 470 nm), matching theradiative blue light from an InGaN-based LED, which emits around 465 nm.Their broad-band emissions are due to a 4f⁶5d¹→4f⁷ transition within theEu²⁺ ion, with the Ca compound emitting at wavelengths ranging fromabout 605-615 nm, Sr at 609-680 nm, and Ba at 570-680 nm. ForM₂Si₅N₈:Eu²⁺ with M restricted to Sr and Ba, the emission band of Eu²⁺successively shifts from orange when M is Sr, and yellow when M is Ba atlow Eu concentrations, to red (up to 680 nm) for high concentrations ofEu.

As taught by Li et al., the excitation spectra are not substantiallydependent on the type of alkaline earth, but the position of theemission bands are. The peak emission bands for a 1 mole percentactivator concentration were 605, 610, and 574 nm, for M=Ca, Sr, and Ba.The shift in the emission band with the nature of the alkaline earth isdue to a difference in the Stokes shift for each of the members, wherethe Stokes shift gradually increases with the sequence Ca>Sr>Ba, andthis trend is predictable if one observes that the relaxation of the4f⁶5d¹ state becomes less restricted when the size of the alkaline-earthion decreases. Further, the Stokes shift increases for as the Euconcentration is increased in all cases.

Aluminonitridosilicates may be derived from nitridosilicates bysubstitutions of aluminum for silicon. A new red phosphor having theformula Ca₂AlSiN₃ has been described by K. Uheda et al. in “Luminescenceproperties of a red phosphor, CaASiN₃:Eu²⁺, for white light-emittingdiodes,” in Electrochemical and solid-state letters, 9 (4) (2006), pagesH22-H25. The crystal structure of the CaAlSiN₃:Eu²⁺ was found to beorthorhombic with a Cmc21 space group, where the unit cell volumeexpanded linearly with an increase in Eu concentration up to at least 20mole percent. The structure is made up of tetrahedra of [SiN₄] and[AlN₄] forming corner sharing six-member rings; rings are combined toform sheets, of which there are two types. The overall structure is madeup of overlaying sheets rotated 180 degrees to one another, forming arigid three-dimensional framework, with the Ca²⁺ ions accommodated incavities in the overlaid planes, and where the Eu²⁺ ions substitute forthe Ca²⁺ ions. Two thirds of the N atoms are coordinated with three Siatoms, and the remaining N atoms are coordinated with two Si atoms. Thisis to be contrasted with the nitridosilicate phosphor CaSiN₂:Eu²⁺described earlier, where all the N atoms are coordinated with two Siatoms. As a result, CaAlSiN₃:Eu²⁺ has a more rigid structure thanCaSiN₂:Eu²⁺.

As taught by Uheda et al., the excitation spectra of thealuminonitridosilicate CaAlSiN₃:Eu²⁺, like the nitridosilicateCa₂Si5N₈:Eu²⁺, shows a broad excitation band that extends to the visibleregion. This feature means that CaAlSiN₃:Eu²⁺ is also suitable forexcitation by a blue or near-UV LED. Under excitation conditions rangingfrom at least about 250 to 500 nm, the luminescence of thisnitridoaluminosilicate shows a single band typical of a 5d-4f transitionof Eu²⁺. Under 405 nm excitation, the phosphor exhibits a peak emissionat about 660 nm, and the emission looks deep red. With an increase in Euconcentration, the emission peak shifts toward longer wavelengths, andquantum output reaches a maximum at about 1.6 mole percent. The quantumoutput is about 1.5 times that of the YAG class of aluminates,(Y,Gd)₃(Al,Ga)₅O₁₂:Ce³⁺, under 460 nm excitation.

Further discussion of the phosphor expressed by the formula(Ca,Eu)AlSiN₃, and described as a “nitride crystalline red fluorescentmaterial,” was disclosed in U.S. Pat. No. 7,253,446 to Sakuma et al.(such phosphors could be described by the formula Ca_(1−p)AlSiN3:Eu²⁺_(p) to quantify europium content). They could be excited over a widerange of light, from violet (about 400 nm) to blue (about 480 nm),though they were preferably (meaning most efficiently) excited at acentral, 450 nm wavelength in that range. X-ray diffraction confirmed acrystalline phase equivalent to CaAlSiN₃. The peak emission of thisphosphor was located at about 650 nm (or slightly longer), with anemission intensity of about 184 percent greater than the YAG reference(Y,Gd)₃Al₅)₁₂:Ce³⁺.

US 2006/0255710 to Mueller-Mach et al. teach a class of phosphormaterials based on rare earth metal-activated luminescence of analuminum-substituted oxonitridosilicate. The phosphor comprises a hostlattice where the main components are silicon, aluminum, nitrogen, andoxygen. The host lattice has a structure comprising stacks of layers of[(Al,Si)₂N_(6/3)(N,O)_(2/2)], where the silicon and aluminum aresurrounded by oxygen and nitrogen in a tetrahedral fashion.

The phosphor described by Mueller-Mach et al. conforms to the generalformula(Ca_(1−x−y−z)Sr_(x)Ba_(y)Mg_(z))_(1−n)(Al_(1−a+b)B_(z))Si_(1−b)N_(3−b)O_(b):RE_(n),where 0≦x≦1; 0≦y≦1; 0≦z≦1; 0≦a≦1; 0≦b≦1; and 0.002≦n≦0.2 and RE isselected from Eu²⁺ and Ce³⁺.

The CIE color coordinates of an Sr-based exemplary phosphor reported byMueller-Mach et al. are x=0.68 and y=0.318, the phosphor having theformula Ca_(0.95)Sr_(0.05)AlSi(N,O)₃:Eu(2%). A similar Ba-based phosphorhaving the formula Ca_(0.95)Ba_(0.05)AlSi(N,O)₃:Eu(2%) has x and ycoordinates 0.676 and 0.323, respectively. The emission peak of theSr-based phosphor is at 657 nm; that of the Ba-based phosphor is 658 nm.When B is substituted for Al, as in the formulaCaAl_(0.98)B_(0.02)Si(N,O)₃:Eu(2%), x and y are 0.667 and 0.323,respectively, and the peak emission is at 650 nm. A higher concentrationof B, as in the formula CaAl_(0.95)B_(0.05)Si(N,O)₃:Eu(2%), has x and yvalues of 0.663 and 0.336, respectively, with a peak emission at 654 nm.For comparison, the compound CaAlSi(N,O)₃:Eu(2%) has x=0.657, y=0.342,and a peak emission at 652 nm.

Mueller-Mach et al. point out advantages of using theseoxonitridoaluminosilicates in conjunction with other phosphors in awhite LED system. The advantages include 1) these red emittingoxonitridoaluminosilicates do not degrade when used in high humidityenvironments, 2) they are stable when driven at high current, oroperated at high temperature, 3) they may be configured to emit a deeperred light (longer wavelength) relative to previous red phosphors, and 4)they may be readily combined with other phosphors, such as the presentyellow-green silicates.

In summary, the present yellow-green silicates may be combined with ared phosphor selected from the group consisting of a nitridosilicate, anoxynitridosilicate, a nitridoaluminosilicate, and anoxynitridoaluminosilicate. Specific examples of these red phosphors areM_(x)Si_(y)N_(z):Eu²⁺ where M is selected from the group consisting ofCa, Sr, Ba, and Zn; and Z=⅔x+ 4/3y;

M₂Si₅N₈:Eu where M is Ca, Sr, and Ba;

CaSiN₂:Eu²⁺

CaAlSiN₃:Eu²⁺; and

(Ca_(1−x−y−z)Sr_(x)Ba_(y)Mg_(z))_(1−n)(Al_(1−a+b)B_(a))Si_(1−b)N_(3−b)O_(b):RE_(n),where 0≦x≦1, 0≦y≦1, 0≦z≦1, 0≦a≦1, 0<b≦1, 0.002≦n≦0.2, where RE isselected from the group consisting of Eu²⁺ and Ce³⁺.

Many modifications of the exemplary embodiments of the inventiondisclosed above will readily occur to those skilled in the art.Accordingly, the invention is to be construed as including all structureand methods that fall within the scope of the appended claims.

1. A white LED comprising: a radiation source configured to emitradiation having a wavelength ranging from about 410 to 500 nm; a greenphosphor having the formula(Sr_(1−x−y)Ba_(x)M_(y))₂SiO₄:Eu²⁺F,Cl,Br,I,S,N,B, where M is at leastone of an element selected from the group consisting of Ca, Mg, Zn, andCd; where F, Cl, Br, I, S, N, B are used in any combination having atotal molar dopant level in the range 0.0001-0.2; and where 0.3≦x≦1;0≦y≦0.5 when M is Ca; 0≦y≦0.1 when M is Mg; and 0≦y≦0.5 when M isselected from the group consisting of Zn and Cd, the green phosphorconfigured to absorb at least a portion of the radiation from theradiation source and emit light with peak intensity in a wavelengthranging from about 500 to 540 nm; a red phosphor selected from the groupconsisting of CaS:Eu²⁺; SrS:Eu²⁺; MgO*MgF*GeO:Mn⁴⁺; a nitridosilicate,an aluminonitridosilicate, an oxynitridosilicate, and anoxynitridoaluminosilicate; M_(x)Si_(y)N_(z):Eu²⁺ where M is selectedfrom the group consisting of Ca, Sr, Ba, and Zn; and Z=⅔x+ 4/3y;M₂Si₅N₈:Eu²⁺, where M is Ca, Sr, and Ba; CaSiN₂:Eu²⁺; CaAlSiN₃:Eu²⁺;(Ca_(1−x−y−z)Sr_(x)Ba_(y)Mg_(z))_(1−n)(Al_(1−a+b)B_(a))Si_(1−b)N_(3−b)O_(b):RE_(n),where 0≦x≦1, 0≦y≦1, 0≦z≦1, 0≦a≦1, 0<b≦1, 0.002≦n≦0.2, and RE is selectedfrom the group consisting of Eu²⁺ and Ce³⁺; and wherein the red phosphoris configured to absorb at least a portion of the radiation from theradiation source and emit light with peak intensity in a wavelengthranging from about 590 to 690 nm.
 2. A white LED comprising: a radiationsource configured to emit radiation having a wavelength ranging fromabout 410 to 500 nm; a yellow phosphor having the formula(Sr_(1−x−y)Ba_(x)M_(y))₂SiO₄:Eu²⁺F,Cl,Br,I,S,N,B, where M is at leastone of an element selected from the group consisting of Ca, Mg, Zn, Cd;where F, Cl, Br, I, S, N, B are used in any combination having a totalmolar dopant level in the range 0.0001-0.2; and where 0.3≦x≦1; 0≦y≦0.5when M is Ca; 0≦y≦0.1 when M is Mg; and 0≦y≦0.5 when M is selected fromthe group consisting of Zn and Cd, the yellow phosphor configured toabsorb at least a portion of the radiation from the radiation source andemit light with a peak intensity in a wavelength ranging from about 540to 590 nm a red phosphor selected from the group consisting of CaS:Eu²⁺;SrS:Eu²⁺; MgO*MgF*GeO:Mn⁴⁺; a nitridosilicate, analuminonitridosilicate, an oxynitridosilicate, and anoxynitridoaluminosilicate; M_(x)Si_(y)N_(z):Eu²⁺ where M is selectedfrom the group consisting of Ca, Sr, Ba, and Zn; and Z=⅔x+ 4/3y;M₂Si₅N₈:Eu²⁺, where M is Ca, Sr, and Ba; CaSiN₂:Eu²⁺; CaAlSiN₃:Eu²⁺;(Ca_(1−x−y−z)Sr_(x)Ba_(y)Mg_(z))_(1−n)(Al_(1−a+b)B_(a))Si_(1−b)N_(3−b)O_(b):RE_(n),where 0≦x≦1, 0≦y≦1, 0≦z≦1, 0≦a≦1, 0<b≦1, 0.002≦n≦0.2, and RE is selectedfrom the group consisting of Eu²⁺ and Ce³⁺; and wherein the red phosphoris configured to absorb at least a portion of the radiation from theradiation source and emit light with peak intensity in a wavelengthranging from about 590 to 690 nm.